Quenching is one of the primary processes to improve mechanical properties in steels, particularly hardness. Quenching is well established for different geometries of individually treated steel components; while in-steam quenching of large diameter continuously cast steel bar has several specific features which are difficult and costly to experimentally optimize. The end-quench Jominy test has been used extensively to study the hardenability of different steel grades. Different numerical, analytical, and empirical models have been developed to simulate the Jominy process and to understand quenching of steels. However, it is not straight forward to translate experimental data from Jominy test on instream quenched large diameter continuously cast products. Therefore, in this work, coupled thermal, mechanical, and metallurgical models were used to simulate the end-quench Jominy test and in-stream quenched industrial round billets with a goal to obtain similarity of experimental structure and properties for both quenched products. For this purpose, finite element analysis (FEA) was employed using the software FORGE (by Transvalor). Used thermophysical properties were generated by JMATPro software. The evolution of microstructure during quenching and resulting hardness were simulated for AISI 4130, and AISI 4140 steel grades. The cooling rates at different positions in the Jominy bar were determined by simulation and compared to experimental. After verification and validation, the FEA simulation was utilized to predict different phases and hardness at different conditions in industry produced round billets. Additionally, relations between Jominy positions and radial positions in the billet were established allowing us to predict structure and properties in inline quenched continuously cast bar having different diameters.

High-alloy steels, like Ferrium C64, are used in powertrain components due to their corrosion resistance and high temperature resistance properties. These steels undergo a tempering temperature that is well above traditional steel, and during this process alloy carbides or compounds form, increasing the materials hardness, mechanical strength, and high temperature resistance properties. In the early stages of tempering, softening occurs due to the formation and coarsening of iron carbide, followed by a hardening as the alloy elements combine to form nano-scale dispersoids. These alloy carbides block the path of dislocations in the grain, strengthening the material. At longer tempering times or high temperatures, the coarsening of these alloy carbides and compounds can cause softening. A predictive material model for the high-tempering response of steels is needed to ensure peak hardening properties are met. For a robust heat treatment model, the material response for every step of the process needs to be modeled. These material properties include austenitization rates and thermal expansion during heating, carbon diffusivity and saturation limits for carburization, phase transformation rates and thermal contraction rates per phase during cooling and quenching, deep-freeze kinetics for further martensitic transformation, tempering kinetics for formation of the tempered martensite phase, and carbide kinetics for formation, coarsening, and size. Additionally, mechanical properties of each phase as a function of carbon need to be defined to ensure the proper mechanical response during and after heat treatment. After the material model is developed it can be used to design and optimize the high-temperature tempering process for any part using the same material.

Thermochemical treatments like carburizing and carbonitriding allow to improve the properties in low-alloyed steels, which depend mainly on the distributions of residual stresses and microstructures. As the fatigue properties depend mainly on the latter, a fundamental understanding must be established regarding their formation during the cooling after the enrichment treatment. This study introduces an experimental and simulation analysis of microstructure and internal stresses evolutions and their couplings. Influence of the carbon and nitrogen enrichments is highlighted. An original experimental technique is introduced to follow in situ by High-Energy XRD the phase transformation kinetics and the evolutions of the internal stresses during cooling, inside laboratory scale samples with C/N composition gradients. The usual trends are confirmed regarding the carburizing: the carbon-enriched case is the last to undergo phase transformations. Due to the phase transformation strains, the surface ends up with compression residual stresses, whereas the center is put in tension. Conversely, for carbonitriding, unusual profiles of microstructures and residual stresses are observed. The presence of nitrogen induces a drastic loss of hardenability in the enriched case. This modifies the chronology of the phase transformations and this leads to tensile residual stresses at the surface for the studied cooling conditions. In the nitrogen-enriched case, a fine microstructure is formed during cooling and retained austenite remains, leading to a lower hardness than in the martensite layer beneath. A coupled thermal, mechanical and metallurgical model predicting the phase transformation kinetics and the evolutions of internal stresses is set up. It takes account of the local carbon and nitrogen concentrations in the case. For carburizing, predictions are in good agreement with experiment. Simulations for carbonitriding achieve to predict the tensile stresses in the nitrogen-enriched case, which are due to the loss of hardenability. In both cases, residual stresses come mostly from phase transformation plasticity strains.

A micro-alloyed 1045 steel was commercially rolled into 54 mm diameter bars by conventional hot rolling at 1000 °C and by lower temperature thermomechanical rolling at 800 °C. The lower rolling temperature refined the ferrite-pearlite microstructure and influenced the microstructural response to rapid heating at 200 °C·s -1 , a rate that is commonly encountered during single shot induction heating for case hardening. Specimens of both materials were rapidly heated to increasing temperatures in a dilatometer to determine the A c1 and A c3 transformation temperatures. Microscopy was used to characterize the dissolution of ferrite and cementite. Continuous cooling transformation (CCT) diagrams were developed for rapid austenitizing temperatures 25 °C above the A c3 determined by dilatometry. Dilatometry and microstructure evaluation along with hardness tests showed that thermomechanical rolling reduced the austenite grain size and lowered the heating temperature needed to dissolve the ferrite. With complete austenitization at 25 °C above the A c3 there was little effect on the CCT behavior.

AISI 8620 low carbon steel is widely used due to its relatively low cost and excellent case hardening properties. The nominal chemistry of AISI 8620 can have a large range, affecting the phase transformation timing and final hardness of a carburized case. Different vendors and different heats of steel can have different chemistries under the same AISI 8620 range which will change the result of a well-established heat treatment process. Modeling the effects of alloy element variation can save countless hours and scrap costs while providing assurance that mechanical requirements are met. The DANTE model was validated using data from a previous publication and was used to study the effect of chemistry variations on hardness and phase transformation timing. Finally, a model of high and low chemistries was executed to observe the changes in hardness, retained austenite and residual stress caused by alloy variation within the validated heat treatment process.

This paper provides an overview of salt quench hardening and how it compares with oil quenching. It explains how salt quenching promotes hardenability, ductility, and strength as well as distortion control, heat extraction, and process reduction. It discusses equipment layout configurations, NFPA guidelines and safety practices, and salt quench processes for austempering, marquenching, and neutral hardening applications.

This paper presents a method for calculating quench severity based on hardness profile matching. The new method has the potential to eliminate the need for Jominy end-quench testing as required in the traditional Kern approach. To assess the accuracy of the proposed method, a test bar and Jominy bar were machined from 2-in. bar stock and heat treated in accordance with ASTM A255. The test bar was quenched in a draft-tube system with a water velocity of 6 ft/s. An excel workbook was programmed to calculate the quenched hardness profile based on prior austenite grain size and steel chemistry. The calculations were in good agreement with measured Jominy hardness as were the quench severities determined by the Kern method and the proposed hardness profile matching technique.

Modeling of as-tempered hardness in steel is essential to understanding final properties of heat-treated components. Most of the tempering mathematical models derive a tempering parameter using Hollomon-Jaffe formulation. Some recent models incorporate chemical composition into the general Hollomon-Jaffe relationship. This paper compares model predictions with a substantial set of actual tempered Jominy End Quench bars and the hardness data from them. Improvements to the models and direction for future work are discussed.

A method of predicting tempered hardness of mixed microstructures has been formulated, which uses the quenched hardness and steel chemistry as independent variables. This calculation is based upon a method first proposed in 1947 by Crafts and Lamont for mixed microstructures and modified using the 1977 chemistry-based, tempered martensite hardness calculation of Grange, Hribal, and Porter. Tempered hardness predictions were examined using Jominy end-quench bars tempered between 204°C (400°F) and 649°C (1200°F). The measured Jominy hardness after tempering was used to make adjustments to the Crafts and Lamont parameters used in the hybrid model. Both plain carbon (SAE 1045) and low alloy (SAE grades 8620, 4130, 4142, and 5160) were used to evaluate the chemistry-based hardness prediction. In combination with a ASTM A255 Jominy hardenability calculation, the proposed calculation can be used to predict the quenched and tempered hardness profile of a round bar based upon chemistry, quench severity, and tempering temperature.

An empirical model has been developed by studying the rate of case formation for various materials. This model uses the relationship observed between material hardenability and case rate. Material hardenability is based on a modified version of Ideal Diameter by using the nominal steel composition with the exception of holding carbon constant at 0.40% (a rough estimation of the carbon level required for effective case depth). It predicts the level of diffusion needed to meet specification requirements and adjust parameters to optimize process design and resulting product characteristics. Inputs needed for process control are the equivalent diffusion number and a material classification. All times, temperatures, carbon set points and level off parameters are automatically downloaded to the equipment for process execution.

Intensive water quenching (IQ) is not a new technology. It goes back over 50 years in Russia and 18 years in the USA. The use of IQ after induction through-heating on “Limited Hardenability” Steels to eliminate the long carburization cycle for case hardened parts is one of many successful applications of IQ.

Previous work was reported on the induction hardening process for a 1541 steel axle shaft. This presentation compares the previous results with the stress formation dynamics in the same shaft made from steels with lower hardenability. Hardened using a scan heating method and a trailing PAG spray quench, several steels having lower hardenability were modeled using the same heating schedule so that the depth of austenite formation is similar in all cases. During spray quenching, the hardened case is shallower as steel hardenability is reduced. This leads to differences in the magnitude of compressive and tensile stresses and their distributions. In turn, the potential for internal cracking is reduced as the stress transition zone is altered by the thickness of the diffusive phase layer between the martensitic case and the ferrite-pearlite core of the shaft. The next step is to investigate these effects on the torque carrying ability of the shaft.

A new technology has been introduced to the North American market as a potential replacement for conventional gas carburizing. This new approach, called Through Surface Hardening (TSH) technology, utilizes a low hardenability (LH) steel and induction hardening to create a contoured hardened pattern, similar to a traditional gas carburizing process. In this study, TSH-processed and conventional gas-carburized SAE 8620 fatigue samples were subjected to reverse torsional loading, generating comparative stress to cycle curves. This paper outlines the torsional fatigue performance and metallurgical characteristics of each process type.

Gas quench, with advantages such as reducing distortion and residual stress, is developing rapidly with the intent to replace liquid quench. Medium and high hardenability steels are needed for gas quench, since the quenching power is lower compared to liquid quench 1 . The traditional Jominy end quench test and Grossmann test, designed for liquid quench steel hardenability, didn’t properly determine the hardenability of high alloyed steels. In order to determine gas quench steel hardenability, a new test is required. In this paper, a critical heat transfer coefficient (HTC) test based on the Grossmann test is proposed. Critical HTC, a concept like critical diameter, was successfully proved to describe the gas quench hardenability of steel. The critical HTC of AISI 4140 steel is 430 W/m 2 C and the critical HTC of AISI 52100 steel is 820 W/m 2 C, which reveals that the gas quench hardenability of 4140 is better than 52100. In the paper, the critical HTC test requirements are presented and discussed.

Developing heat treat systems and control plans that produce consistent direct harden (quench and temper) results with a high percent martensite and the corresponding proper mechanical properties is challenging for large components or large batch sizes. In this study, large section bars in alloys suitable for water quenching were austenitized and quenched under controlled flow conditions. The bars were primarily examined by several as-quenched hardness versus depth traverses in order to be sure localized non-martensitic regions (soft areas) would be detected. The tests allowed for some key insights into defining the adequacy of direct harden water quench systems, including the idea of agitation thresholds required for each alloy grade or hardenability level to prevent soft spots (spotty hardening) on large section steel components.

Press quenching is an effective method to improve the strength and control the distortion of auto gears. However, it can be challenging to understand, predict, and further minimize the deformation of circular-arc bevel gears in industrial applications because of multiple influencing factors. This paper reports on work to build a comprehensive model with phase changes to reproduce the gear quenching process with consideration of the quenching machine, process parameters, and variation of steel compositions. The phase content and temperature history predicted by the model agree with the gear-quenching experimental results.

Hot isostatic pressing or HIP has been used for diffusion bonding, casting densification, and powder consolidation. Continuous advances in HIP equipment design have allowed increasingly rapid cooling, recently reaching a point where true high-pressure gas quenching is now possible within the HIP unit. This capability further enables the integration of a heat treat and HIP processing. Within the heat treat industry, high pressure gas quenching has been an area of significant development, however, where typical high pressure gas quenching equipment offers quench pressures up to 15 or 20 bar, common HIP pressures are 1000 bar or higher. The ability to quench from HIP pressures appears to offer heat treat options not previously available. This paper examines ultra-high pressure gas quenching (from 1500 bar) within the HIP unit from a heat treating point of view using AISI 4140 steel, a well characterized, medium hardenability alloy, comparing the properties and microstructure of ultra-high pressure gas/HIP quenched steel to conventional water and oil quenched results.

In the last centuries carbonitriding was mainly used to enhance the hardenability of unalloyed steels. IWT developed gas-carbonitriding and low-pressure-carbonitriding processes to increase fatigue behavior and quality compared to case hardening. For example, modern gas-carbonitriding processes make it possible to extend materials ́ strength, so that the limit of use of a given alloy can be expanded. The paper shows examples for the treatment of ball bearing and case hardening steels. The treatment results in microstructures, which are unusual, compared with conventional heat treated parts. They are characterized by high amounts of retained austenite and carbonitride precipitations. By a controlled process, which has been developed in cooperation with PROCESS-ELECTRONIC, it is possible to adjust surface carbon- and nitrogen content independently. Low pressure carburized parts have the advantage that no internal oxidation occurs. So they have the potential of leading to a higher strength. Nowadays LP-carburizing is used in a wide range, whereas LP-carbonitriding processes are at a starting point. In this paper possibilities and limitations of this process are shown. So, inline controlling of LP-processes in a classical way is not possible, but simulation guided process control. The paper will give examples for LP-carbonitriding processes and the resulting microstructure.