Patent Application
20210047703
This application claims the foreign priority benefit of Czech Patent Application Serial No. PV 2019-537 entitled “METHOD OF THERMOMECHANICAL TREATMENT OF SEMI-FINISHED PRODUCTS OF HIGH-ALLOY STEEL,” filed Aug. 16, 2019, the entire disclosure of which is incorporated herein by reference.
This invention generally relates to a method for the thermomechanical treatment of semi-finished products of high-alloy steel.
When produced by conventional metallurgy, high-alloy tool steels contain large sharp-edged M7C3 carbides, which remain stable even at high temperatures. There is substantially no way of converting these carbides by means of conventional heat treatment to a more favourable morphology, i.e., to finer and more uniformly dispersed carbides. Since large sharp-edged primary carbides considerably reduce toughness, this kind of steel must be produced by powder metallurgy, which can obviate the risk of formation of large chromium carbides. A method of removing carbides is described in U.S. Pat. No. 10,378,075.
One or more embodiments of the present invention generally concern a method for the thermomechanical treatment of semi-finished products of high-alloy steel. Generally, the method comprises: (a) heating a semi-finished steel product to a temperature of at least 1200° C. to form a heated product; (b) cooling the heated product to form a first cooled product; (c) reheating the first cooled product to a forming temperature to thereby produce a formed product; and (d) cooling the formed product to ambient temperature.
The invention generally relates to a method for the thermomechanical treatment of semi-finished products of high-alloy steel, in which the steel semi-finished product is heated above 1200° C., after which the semi-finished product is cooled and then reheated to a forming temperature, at which the semi-finished product is formed and then cooled to ambient temperature. Chromium carbides only dissolve at temperatures above the solidus. Therefore, a technique based on semi-solid-processing may be used for removing these carbides from high-alloy tool steels. During semi-solid processing, the material exists as a mixture of liquid and solid phases. When in the semi-solid state, the material exhibits thixotropy and can be shaped by thixoforming.
Thixoforming is a technique which can be used to produce intricate-shape parts in a single forming cycle. It creates microstructures characterized by polyhedral grains of super-saturated austenite embedded in a carbide network. The network consists of lamellar carbides and austenite. Consequently, no large sharp-edged primary carbides remain in the structure. In such structures, austenite possesses an extraordinary thermal stability. Its thermal decomposition only starts at a temperature as high as 500° C. The decomposition is complete during annealing at 550 to 600° C. Austenite per se is ductile, but the carbide network lacks the ability to undergo sufficient plastic deformation at room temperature (RT). Nevertheless, materials with these structures can be formed successfully by compressive deformation. It has been verified experimentally that they can also be formed at high temperatures between 1000° C. and the solidus.
At an appropriate temperature, the carbide network can be broken up by forming at an appropriate magnitude and intensity of deformation, and carbides can be dispersed uniformly throughout the austenitic matrix. After cooling, these carbides can remain dispersed, and therefore contribute to the strength of the resulting structure. These carbides may retard austenite grain growth in the course of deformation at high temperatures. Deformation and temperature can cause these carbides to partially dissolve. After reprecipitation, the carbides can contribute to additional strengthening of the matrix. To achieve optimal properties, the matrix can be altered by additional heat treatment, such as quenching and tempering, or even quenching and partitioning. If mechanical working finishes under appropriate conditions, a structure with fine martensite is obtained.
An unconventional thermomechanical treatment route was used to remove large sharp-edged primary chromium carbides from tool steels, in which these carbides normally form during solidification at the metallurgical stage of production and are impossible to remove by classical heat treatment. The underlying principle is to use conversion to the semi-solid state to transform the initial microstructure to polyhedral austenite embedded in a carbide-austenite network, and then use forming to break up this network and produce a fine microstructure of a martensitic-austenitic constituent and fine chromium carbide precipitates. The semi-solid condition is necessary to achieve a temperature at which primary sharp-edged chromium carbides dissolve. By this means, the carbides can be converted to an austenitic-carbidic structure, which can be hot-formed, and, using plastic deformation, the carbide network can be fragmented, and the carbides dispersed uniformly.
One or more embodiments concern a method for the thermomechanical treatment of semi-finished products of high-alloy steel. In various embodiments, the method comprises: (a) heating a semi-finished steel product to a temperature of at least 1200° C. to form a heated product; (b) cooling the heated product to form a first cooled product; (c) reheating the first cooled product to a forming temperature to thereby produce a formed product; and (d) cooling the formed product to ambient temperature. During the heating of step (a), the semi-finished steel product may be held at 1200° C. for at least 15 minutes. Furthermore, in various embodiments, the semi-finished steel product is cooled to a temperature between 20° C. and 1100° C. during the cooling of step (b). Moreover, in various embodiments, the forming temperature of the semi-finished steel product is between 1050° C. and 1100° C. and the semi-finished steel product may be held at this temperature for at least 1.5 minutes.
The invention can be used in metallurgical processing and in the manufacture of parts, primarily for the machinery industry.
This invention can be further illustrated by the following examples of embodiments thereof, although it will be understood that these examples are included merely for the purposes of illustration and are not intended to limit the scope of the invention unless otherwise specifically indicated.
X210Cr12 is a high-carbon and high-chromium steel that contains the composition shown in TABLE 1. X210Cr12 was developed for applications in punching and pressing tools, mainly for heavy-duty punches and highly-complex progressive and combination tools. It is a suitable material for blades for shearing wires, sheet, and other stock. Its initial annealed microstructure contains large sharp-edged primary chromium carbides and very fine cementite embedded in a ferritic matrix. In order to find the appropriate process parameters, it was necessary to identify the freezing range and the dissolution temperature of the chromium carbides.
It was found that the material retains a stable ferrite-cementite microstructure up to 758° C. The material begins to melt at 1225° C. and becomes fully melted at 1373° C. The liquid fraction vs. temperature curve shows that primary chromium carbides dissolve at 1255° C.
To obtain carbide precipitates with an optimal distribution, sizes, and morphology, and microstructures with optimal austenite grain sizes and martensite volume fractions, a number of treatment parameters had to be optimized, starting with the temperature of heating to semi-solid state. To break up the lamellar network and initiate recrystallization, the material had to be worked using a large amount of deformation. Open-die forging in a hydraulic press was used. As the material was heated to semi-solid state, the semi-finished product was enclosed in a container made of low-carbon steel. This simplified the handling of the partially melted material and made the temperature field more homogeneous. A container with a diameter of 30 mm, wall thickness of 6 mm, and length of 55 mm was made of SJ355 low-carbon steel, whose melting temperature was above 1400° C. The semi-finished products were heated in a furnace with no protective atmosphere. Flat dies were used for forming. Several different treatment routes were tested, as shown in TABLE 2.
Routes 1-3 involved a heating temperature of 1265° C. and a heating time of 15 minutes. At this temperature, all primary chromium carbides were dissolved, and the structure comprised a liquid phase and austenite. According to calculations, the liquid fraction was 30%. The variants included quenching in water to 500° C. (routes 1 and 2) and to room temperature (route 3), followed by reheating to the forming temperature, either at 1050° C. or 1110° C., and holding for 5 minutes. The semi-finished products were upset to a half height in a single operation.
In the next route, the heating temperature was reduced to 1220° C. This temperature was just below the calculated solidus temperature. At this temperature, the microstructure still contained about 8% of M7C3 carbides. In route 4, quenching to 600° C. was performed and followed by reheating in a furnace to a forming temperature of 1050° C. The semi-finished product was first upset to a half height, then drawn out to 50 mm and then upset again to a height of 20 mm.
Another variant (route 5) had the same heating temperature, but involved cooling to no less than 1100° C. followed by forming: upsetting—drawing-out—upsetting—drawing-out. Forming was finished at a temperature below 800° C.
In order to explore the effects of the holding time, route 6 had the holding time extended to 60 minutes. The purpose was to ascertain whether the austenite grains coarsen, whether coarser grains affect the morphology of recrystallized grains after forming, and whether a larger proportion of primary chromium carbides dissolve.
In yet another variant (route 7), the heating temperature was reduced further, to 1200° C. At this temperature, there should be no liquid phase in the structure, and therefore comparison could be made between the effects of different liquid fractions on microstructural evolution. Upon heating, the microstructure comprised a mixture of austenite and 9% of carbides. The heating temperature and times were 1240° C. and 15 minutes and 60 minutes, respectively. This temperature was close to the temperature of complete dissolution of primary chromium carbides. Nevertheless, their amount is still approximately 7% in the structure. Cooling to 900° C. was performed, followed by reheating to the forming temperature of 1080° C.
In order to characterize the effect of higher liquid fraction on microstructural evolution, route 10 involved the highest heating temperature, 1280° C. It was expected to lead to complete dissolution of carbides and to melting of austenite.
X155CrVMol21 is a chromium-molybdenum-vanadium hypereutectoid cold-work tool steel, which contains the composition depicted in TABLE 3. It can be oil-quenched or air-quenched and offers excellent hardenability, better than X210Cr12 steel. Generally, X155CrVMol21 has high wear resistance and sustains high compressive loads. It is also used for blanking tools operating under severe loads, up to a thickness of approximately 10 mm, and for trimming tools for forged parts, as well as for punching, drawing and extrusion tools. Other applications for X155CrVMol21 include hot-forming tools, where high hardness and wear resistance are required, and cutting tools for machining low-strength metals.
The semi-finished product was enclosed in a container from SJ355 low-carbon steel, whose melting temperature is above 1400° C. Due to this arrangement, it was possible to handle the partially-melted material between furnaces. Four different treatment routes were carried out, as shown in TABLE 4. First, two different heating temperatures, 1265° C. and 1300° C., were tested, with time at temperature in the furnace of 15 minutes. At 1265° C., the material contained approximately 20% liquid phase and at 1300° C. it contained approximately 31% liquid phase. After holding at temperature, quenching in water to room temperature was performed. In route 3, heating at 1265° C. was followed by quenching in water for 2 seconds. Using a pyrometer, the temperature of the specimen was found to be 930-950° C. Then, reheating to 1080° C. and holding for 1.5 minutes was carried out. At this temperature, the material began to enter the austenite region again. After holding for 1.5 minutes, the specimen was quenched in water. This holding time represents the time period in which forging in a hydraulic press is performed in subsequent routes.
It should be understood that the following is not intended to be an exclusive list of defined terms. Other definitions may be provided in the foregoing description, such as, for example, when accompanying the use of a defined term in context.
As used herein, the terms “a,” “an,” and “the” mean one or more.
As used herein, the term “and/or,” when used in a list of two or more items, means that any one of the listed items can be employed by itself or any combination of two or more of the listed items can be employed. For example, if a composition is described as containing components A, B, and/or C, the composition can contain A alone; B alone; C alone; A and B in combination; A and C in combination, B and C in combination; or A, B, and C in combination.
As used herein, the terms “comprising,” “comprises,” and “comprise” are open-ended transition terms used to transition from a subject recited before the term to one or more elements recited after the term, where the element or elements listed after the transition term are not necessarily the only elements that make up the subject.
As used herein, the terms “having,” “has,” and “have” have the same open-ended meaning as “comprising,” “comprises,” and “comprise” provided above.
As used herein, the terms “including,” “include,” and “included” have the same open-ended meaning as “comprising,” “comprises,” and “comprise” provided above.
The present description uses numerical ranges to quantify certain parameters relating to the invention. It should be understood that when numerical ranges are provided, such ranges are to be construed as providing literal support for claim limitations that only recite the lower value of the range as well as claim limitations that only recite the upper value of the range.
For example, a disclosed numerical range of 10 to 100 provides literal support for a claim reciting “greater than 10” (with no upper bounds) and a claim reciting “less than 100” (with no lower bounds).
The preferred forms of the invention described above are to be used as illustration only, and should not be used in a limiting sense to interpret the scope of the present invention. Modifications to the exemplary embodiments, set forth above, could be readily made by those skilled in the art without departing from the spirit of the present invention.
The inventors hereby state their intent to rely on the Doctrine of Equivalents to determine and assess the reasonably fair scope of the present invention as it pertains to any apparatus not materially departing from but outside the literal scope of the invention as set forth in the following claims.
| Number | Date | Country | Kind |
|---|---|---|---|
| PV 2019-537 | Aug 2019 | CZ | national |
